CN109868346A - A kind of BH2Value is greater than the 800MPa rank dual phase steel production method of 70MPa - Google Patents
A kind of BH2Value is greater than the 800MPa rank dual phase steel production method of 70MPa Download PDFInfo
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Abstract
The present invention provides a kind of BH2Value is greater than the 800MPa rank dual phase steel production method of 70MPa, the method mainly by by carbon content control in molten steel in 0.09-0.11%, Nb content is controlled in 0.04-0.05%, optimize hot rolling, curling, cold-rolling process, further control continuous annealing process are as follows: the strip is heated to 250-270 DEG C through 15-20s, 820-840 DEG C is heated to through 270-290s again, keep the temperature 90-110s, then 620-640 DEG C is cooled in 26-30s, 310-330 DEG C is cooled to through 5-7s again, 270-290 DEG C is cooled to through 250-260s again, it then cools to room temperature, improve the BH of 800MPa rank dual phase steel2Value improves vehicle overall security so that the body of a motor car bending resistance of dependency structure safety member and energy absorption ability after paint baking is higher with respect to common product.
Description
Technical field
The invention belongs to metal material processing technical fields, and in particular to a kind of BH2Value is greater than the 800MPa rank of 70MPa
Dual phase steel production method.
Background technique
800MPa rank dual phase steel is with the cooperation of its low yield strength ratio, high initial manufacture hardening rate, good strength and ductility
The advantages that, a kind of good New Type Punching Steel of forming property is had evolved into, Hyundai Motor front longitudinal beam, A, B column, rear guarantor are become
The first choice material of the safety members such as crossbeam.Since Modern Automobile Body will always pass through drying in paint baking, including vehicle body baking
It is painted with bonding.According to the luxury level of different brackets quality requirement, the quantity of skin of paint and automobile, this process can be more
Secondary progress.This baking treatment process not only facilitates painting work, and the yield strength of dual phase steel generally rises after baking
20-60MPa, the bending resistance and energy-absorbing effect that the raising of intensity will increase part are (studies have shown that the every raising of yield strength
10MPa, three-point bending peak load improve about 1.2%, and 0.8%) energy-absorbing effect is promoted, improve vehicle overall security.Therefore
Develop a kind of BH2The 800MPa rank two-phase steel product that value stably reaches 70MPa or more has very big practical application meaning.In
State patent CN201410651490.1 discloses " a kind of tensile strength >=780MPa grades of hot-rolled dual-phase steel and production method ", narration
Tensile strength >=780MPa, elongation percentage >=15%, a kind of dual phase steel production method of yield tensile ratio≤0.70, this patent right are wanted
The feature asked are as follows: cover insulation cover in moderate soak section, and reduce strip cooling velocity, can effectively prevent the production of pearlitic transformation
It is raw, it realizes the yield strength and yield tensile ratio of product, does not refer to dual phase steel BH2Property problem.
Summary of the invention
In view of this, the present invention provides a kind of BH2Value is greater than the 800MPa rank dual phase steel production method of 70MPa.It is logical
It crosses and controls reasonable ingredient, hot rolling technology, cold rolling reduction ratio, annealing process, improve the BH of 800MPa rank dual phase steel2Value reaches
70MPa or more, so that the body of a motor car bending resistance of dependency structure safety member and energy absorption ability after paint baking is opposite
Common product is higher, improves vehicle overall security.
First aspect present invention provides a kind of BH2Value is greater than the 800MPa rank dual phase steel production method of 70MPa, step
Include:
S1, molten steel casting obtain slab；By percentage to the quality, in the molten steel carbon content control in 0.09-0.11%,
Nb content is controlled in 0.04-0.05%；
S2, slab obtained by step S1 is successively passed through into hot rolling, curling, cold rolling；
S3, strip obtained by step S2 is subjected to continuous annealing treatment, the continuous annealing process step includes: by the band
Steel is heated to 250-270 DEG C through 15-20s, then is heated to 820-840 DEG C through 270-290s, keeps the temperature 90-110s, then 26-30s
It is inside cooled to 620-640 DEG C, then is cooled to 310-330 DEG C through 5-7s, then be cooled to 270-290 DEG C through 250-260s, it is then cold
But to room temperature.
Present component control requires carbon content to be strict controlled between 0.09-0.11%, and Nb content must be strictly controlled
Between 0.04-0.05%, purpose be provide enough carbonization Nb precipitates make in subsequent heating and cooling procedure it is double
Retain enough dissolved carbon contents in phase steel ferritic phase.
Subsequent anneal is further heated to 820-840 DEG C for 270-290 seconds, is cooled to after keeping the temperature 90-110s through 26-30 seconds
It 620-640 DEG C, realizes that back dissolving occurs in annealing process for niobium carbide precipitate, will not be analysed completely after cooling since temperature is lower
Out, guarantee that dissolved carbon content level reaches 25ppm or more in two-phase steel organization ferrite, realizes BH2Value > 70MPa.
Preferably, in step S1, the chemical component of the molten steel includes: C:0.09-0.11% by percentage to the quality；
Mn:2.0-2.2%；Si≤0.5%；P≤0.015%；S≤0.005；Alt:0.02-0.06%, Nb:0.04-0.05%, Cr:
0.4-0.6%, surplus are Fe and inevitable impurity.
Preferably, in step S2, heating temperature is controlled in the hot rolling technology: 1170-1230 DEG C；Finishing temperature: 860-
900℃。
More preferred, in step S2, the coiling temperature is 640-680 DEG C.
Preferably, in step S2, the reduction ratio of the cold rolling is 65-70%.Certain cold rolling reduction ratio is then continuous
The driving force of annealing recrystallization, and the number of Recrystallization nucleation point determined.The present invention, will according to different steel strip thickness specifications
Cold rolling reduction ratio, which substantially controls, is being greater than 65% level.
Preferably, in step S3, the continuous annealing process is in H2And N2It is carried out under mixed-gas atmosphere.
More preferred, in step S3, described be cooled to room temperature is cooled down using water-cooling pattern.
It is further preferred that dissolved carbon content is in 25ppm or more in dual phase steel ferrite after cooling in step S3.
It is further preferred that the continuous annealing process step includes: to be heated to the strip through 17s in step S3
260 DEG C, then 830 DEG C are heated to through 280s, 100s is kept the temperature, 630 DEG C are then cooled in 28s, then be cooled to 320 DEG C through 6.4s,
280 DEG C are cooled to through 256s again, is then water-cooled to room temperature.
Second aspect of the present invention provides the BH that aforementioned production method is prepared2Value is greater than the 800MPa rank of 70MPa
Dual phase steel.
Compared with prior art, the invention has the following advantages that the present invention is contained by optimal control carbon content and Nb element
Amount ensure that dissolved carbon content reaches in dual phase steel ferrite using being quickly cooled to 630 DEG C after recrystallization high annealing soaking
25ppm or more improves two-phase steel product BH2It is worth to 70MPa or more.By to the techniques such as hot rolling, cold rolling and continuous annealing into
On the basis of row optimization, dual phase steel BH produced2Be worth stability contorting 70MPa or more 800MPa rank dual phase steel, with
After be made after part entrucking that bending resistance and energy absorption ability are mutually due for promotion after body of a motor car paint baking, improve vehicle
Overall security has very big practical application meaning.
Detailed description of the invention
Attached drawing 1 is general technology and produces 800MPa rank dual phase steel BH after using the method for the present invention2It is worth comparison diagram, uses
BH2 value reaches 75MPa under the non-formation state of two-phase steel product after the method for the present invention.
Attached drawing 2 is that general technology produces dual phase steel and using production 800MPa rank dual phase steel in-fighting after the method for the present invention
Snock peak height comparison diagram is higher than general two-phase steel product using two-phase steel product dissolved carbon content after the method for the present invention, reaches
25ppm。
Specific embodiment
To facilitate the understanding of the present invention, present invention work more comprehensively, is meticulously described below in conjunction with embodiment, but this hair
Bright protection scope is not limited to embodiment in detail below.
Unless otherwise defined, all technical terms used hereinafter and the normally understood meaning of those skilled in the art
It is identical.Technical term used herein is intended merely to the purpose of description specific embodiment, is not intended to the limitation present invention
Protection scope.For example, room temperature can refer to the temperature in 10~35 DEG C of sections.
Unless otherwise specified, various raw material, reagent, the instrument and equipment etc. used in the present invention, can pass through
Market is commercially available or can be prepared by existing method.
First aspect present invention provides a kind of BH2Value is greater than the 800MPa rank dual phase steel production method of 70MPa, step
Include:
S1, molten steel casting obtain slab；By percentage to the quality, the chemical component of the molten steel includes: with quality percentage
Than meter, C:0.09-0.11%；Mn:2.0-2.2%；Si≤0.5%；P≤0.015%；S≤0.005；Alt:0.02-
0.06%, Nb:0.04-0.05%, Cr:0.4-0.6%, surplus are Fe and inevitable impurity.
S2, slab obtained by step S1 is successively passed through into hot rolling, curling, cold rolling；Hot rolling technology control heating temperature: 1200 ±
30℃；Finishing temperature: 880 ± 20 DEG C；Coiling temperature: 660 ± 20 DEG C；Cold-rolling process controls cold rolling reduction ratio in 65-70%.
S3, strip obtained by step S2 is entered into furnace medium by H by room temperature2And N2It is carried out in the non-oxidizing atmosphere of composition
Continuous annealing treatment, the continuous annealing process step include: the strip to be heated to 250-270 DEG C through 15-20s, then pass through
270-290s is heated to 820-840 DEG C, keeps the temperature 90-110s, and 620-640 DEG C is then cooled in 26-30s, then cooling through 5-7s
It is cooled to 270-290 DEG C to 310-330 DEG C, then through 250-260s, is then cooled to room temperature, in dual phase steel ferrite after cooling
Dissolved carbon content is in 25ppm or more.
Second aspect of the present invention provides the BH that aforementioned production method is prepared2Value is greater than the 800MPa rank of 70MPa
Dual phase steel.
Below in conjunction with specific embodiment to the BH of the application2Value is greater than the 800MPa rank dual phase steel producer of 70MPa
Method is described in detail.
Embodiment 1
Present embodiments provide a kind of BH2Value is greater than the 800MPa rank dual phase steel production method of 70MPa, and step includes:
S1, molten steel casting obtain slab；By percentage to the quality, the chemical component of the molten steel includes: with quality percentage
Than meter, C:0.10%；Mn:2.1%；Si:0.4%；P:0.015%；S:0.005；Alt:0.04%, Nb:0.05%, Cr:
0.5%, surplus is Fe and inevitable impurity.
S2, slab obtained by step S1 is successively passed through into hot rolling, curling, cold rolling；Hot rolling technology control heating temperature: 1200
℃；Finishing temperature: 880 DEG C；Coiling temperature: 660 DEG C；Cold-rolling process controls cold rolling reduction ratio 65%.
S3, strip obtained by step S2 is entered into furnace medium by H by room temperature2And N2It is carried out in the non-oxidizing atmosphere of composition
Continuous annealing treatment, the continuous annealing process step include: the strip to be heated to 260 DEG C through 17s, then heat through 280s
To 830 DEG C, 100s is kept the temperature, 630 DEG C are then cooled in 28s, then be cooled to 320 DEG C through 6.4s, then be cooled to 280 through 256s
DEG C, then it is water-cooled to room temperature.It is as shown in Table 1 and Fig. 1, Fig. 2 according to dual phase steel results of property after above-mentioned process, as right
Than conventional 800MPa rank two-phase Steel Properties being also tested, test result is as shown in Table 1 and Fig. 1, Fig. 2.
Steel Properties contrast table after the pre-stretching of 1 dual phase steel of table and baking
The dual phase steel BH produced using the method for the present invention2It is worth stability contorting in 70MPa or more, is being subsequently formed into part entrucking
It is mutually due for promotion by bending resistance after body of a motor car paint baking and energy absorption ability, improves vehicle overall security.
Embodiment 2
Present embodiments provide a kind of BH2Value is greater than the 800MPa rank dual phase steel production method of 70MPa, and step includes:
S1, molten steel casting obtain slab；By percentage to the quality, the chemical component of the molten steel includes: with quality percentage
Than meter, C:0.11%；Mn:2.1%；Si:0.5%；P:0.013%；S:0.005；Alt:0.05%, Nb:0.04%, Cr:
0.6%, surplus is Fe and inevitable impurity.
S2, slab obtained by step S1 is successively passed through into hot rolling, curling, cold rolling；Hot rolling technology control heating temperature: 1220
℃；Finishing temperature: 900 DEG C；Coiling temperature: 670 DEG C；Cold-rolling process controls cold rolling reduction ratio 66%.
S3, strip obtained by step S2 is entered into furnace medium by H by room temperature2And N2It is carried out in the non-oxidizing atmosphere of composition
Continuous annealing treatment, wherein the hydrogen accounts for atmosphere gas percent by volume 15%, and the continuous annealing process step includes:
The strip is heated to 255 DEG C through 20s, then is heated to 840 DEG C through 275s, 98s is kept the temperature, 635 DEG C is then cooled in 29s,
318 DEG C are cooled to through 6s again, then is cooled to 275 DEG C through 250s, is then cooled to room temperature, it is solid in dual phase steel ferrite after cooling
Molten carbon content is in 25ppm or more.It is almost the same according to two-phase Steel Properties after above-mentioned process and embodiment 1.
Embodiment 3
Present embodiments provide a kind of BH2Value is greater than the 800MPa rank dual phase steel production method of 70MPa, and step includes:
S1, molten steel casting obtain slab；By percentage to the quality, the chemical component of the molten steel includes: with quality percentage
Than meter, C:0.09%；Mn:2.0%；Si:0.5%；P:0.015%；S:0.005；Alt:0.02%, Nb:0.04%, Cr:
0.4%, surplus is Fe and inevitable impurity.
S2, slab obtained by step S1 is successively passed through into hot rolling, curling, cold rolling；Hot rolling technology control heating temperature: 1180
℃；Finishing temperature: 870 DEG C；Coiling temperature: 650 DEG C；Cold-rolling process controls cold rolling reduction ratio 65%.
S3, strip obtained by step S2 is entered into furnace medium by H by room temperature2And N2It is carried out in the non-oxidizing atmosphere of composition
Continuous annealing treatment, wherein the hydrogen accounts for atmosphere gas percent by volume 10%, and the continuous annealing process step includes:
The strip is heated to 265 DEG C through 16s, then is heated to 820 DEG C through 285s, 95s is kept the temperature, 625 DEG C is then cooled in 26s,
320 DEG C are cooled to through 7s again, then is cooled to 285 DEG C through 260s, then water cooling to room temperature.It is solid in dual phase steel ferrite after cooling
Molten carbon content is in 25ppm or more.It is almost the same according to two-phase Steel Properties after above-mentioned process and embodiment 1.
Although preferred embodiments of the present invention have been described, it is created once a person skilled in the art knows basic
Property concept, then additional changes and modifications may be made to these embodiments.So it includes excellent that the following claims are intended to be interpreted as
It selects embodiment and falls into all change and modification of the scope of the invention.
Obviously, various changes and modifications can be made to the invention without departing from essence of the invention by those skilled in the art
Mind and range.In this way, if these modifications and changes of the present invention belongs to the range of the claims in the present invention and its equivalent technologies
Within, then the present invention is also intended to include these modifications and variations.
Claims (10)
1. a kind of BH2Value is greater than the 800MPa rank dual phase steel production method of 70MPa, and step includes:
S1, molten steel casting obtain slab；By percentage to the quality, carbon content control contains in 0.09-0.11%, Nb in the molten steel
Amount control is in 0.04-0.05%；
S2, slab obtained by step S1 is successively passed through into hot rolling, curling, cold rolling；
S3, strip obtained by step S2 is subjected to continuous annealing treatment, the continuous annealing process step includes: to pass through the strip
15-20s is heated to 250-270 DEG C, then is heated to 820-840 DEG C through 270-290s, keeps the temperature 90-110s, then cold in 26-30s
But to 620-640 DEG C, then through 5-7s it is cooled to 310-330 DEG C, then is cooled to 270-290 DEG C through 250-260s, be subsequently cooled to
Room temperature.
2. BH as described in claim 12Value is greater than the 800MPa rank dual phase steel production method of 70MPa, it is characterised in that: step
In rapid S1, the chemical component of the molten steel includes: C:0.09-0.11% by percentage to the quality；Mn:2.0-2.2%；Si≤
0.5%；P≤0.015%；S≤0.005；Alt:0.02-0.06%, Nb:0.04-0.05%, Cr:0.4-0.6%, surplus are
Fe and inevitable impurity.
3. BH as described in claim 12Value is greater than the 800MPa rank dual phase steel production method of 70MPa, it is characterised in that: step
In rapid S2, heating temperature is controlled in the hot rolling technology: 1170-1230 DEG C；Finishing temperature: 860-900 DEG C.
4. BH as claimed in claim 32Value is greater than the 800MPa rank dual phase steel production method of 70MPa, it is characterised in that: step
In S2, the coiling temperature is 640-680 DEG C.
5. BH described in claim 12Value is greater than the 800MPa rank dual phase steel production method of 70MPa, it is characterised in that: step
In S2, the reduction ratio of the cold rolling is 65-70%.
6. BH described in claim 12Value is greater than the 800MPa rank dual phase steel production method of 70MPa, it is characterised in that: step S3
In, the continuous annealing process is in H2And N2It is carried out under mixed-gas atmosphere.
7. BH as claimed in claim 62Value is greater than the 800MPa rank dual phase steel production method of 70MPa, it is characterised in that: step
In rapid S3, described be cooled to room temperature is cooled down using water-cooling pattern.
8. BH as claimed in claim 72Value is greater than the 800MPa rank dual phase steel production method of 70MPa, it is characterised in that: step
In rapid S3, dissolved carbon content is in 25ppm or more in dual phase steel ferrite after cooling.
9. BH as claimed in claim 62Value is greater than the 800MPa rank dual phase steel production method of 70MPa, it is characterised in that: step
In rapid S3, the continuous annealing process step includes: the strip to be heated to 260 DEG C through 17s, then be heated to 830 through 280s
DEG C, 100s is kept the temperature, 630 DEG C are then cooled in 28s, then be cooled to 320 DEG C through 6.4s, then be cooled to 280 DEG C through 256s, then
It is cooled to room temperature.
10. the BH being prepared using production method described in any one of claim 1-9 claim2Value is greater than 70MPa's
800MPa rank dual phase steel.
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| CN201910209270.6A CN109868346B (en) | 2019-03-19 | 2019-03-19 | BH2Production method of 800MPa grade dual-phase steel with value more than 70MPa |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114279829A (en) * | 2021-11-19 | 2022-04-05 | 邯郸钢铁集团有限责任公司 | Method for detecting high-speed tensile curve of quenching distribution steel |
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| CN101942603A (en) * | 2010-09-28 | 2011-01-12 | 北京科技大学 | 600 MPa-grade ultra-low-silicon cold-rolled hot-galvanized dual-phase steel and preparation process thereof |
| CN102747275A (en) * | 2012-07-23 | 2012-10-24 | 武汉钢铁(集团)公司 | Cold-rolled dual-phase steel with high strain-strengthening performance and method for producing same |
| CN108517468A (en) * | 2018-05-24 | 2018-09-11 | 山东钢铁集团日照有限公司 | A kind of economical cold-rolled biphase steel and its production method of steel multistage |
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- 2019-03-19 CN CN201910209270.6A patent/CN109868346B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101942603A (en) * | 2010-09-28 | 2011-01-12 | 北京科技大学 | 600 MPa-grade ultra-low-silicon cold-rolled hot-galvanized dual-phase steel and preparation process thereof |
| CN102747275A (en) * | 2012-07-23 | 2012-10-24 | 武汉钢铁(集团)公司 | Cold-rolled dual-phase steel with high strain-strengthening performance and method for producing same |
| CN108517468A (en) * | 2018-05-24 | 2018-09-11 | 山东钢铁集团日照有限公司 | A kind of economical cold-rolled biphase steel and its production method of steel multistage |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN114279829A (en) * | 2021-11-19 | 2022-04-05 | 邯郸钢铁集团有限责任公司 | Method for detecting high-speed tensile curve of quenching distribution steel |
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